EP2942414B1 - Dicke, harte stahlplatte mit hoher zugfestigkeit und herstellungsverfahren dafür - Google Patents

Dicke, harte stahlplatte mit hoher zugfestigkeit und herstellungsverfahren dafür Download PDF

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Publication number
EP2942414B1
EP2942414B1 EP14763386.1A EP14763386A EP2942414B1 EP 2942414 B1 EP2942414 B1 EP 2942414B1 EP 14763386 A EP14763386 A EP 14763386A EP 2942414 B1 EP2942414 B1 EP 2942414B1
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steel plate
steel
toughness
plate thickness
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English (en)
French (fr)
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EP2942414A4 (de
EP2942414A1 (de
Inventor
Shigeki KITSUYA
Naoki Matsunaga
Katsuyuki Ichimiya
Kazukuni Hase
Shigeru Endo
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to thick high-toughness high-strength steel plates with excellent strength, toughness and weldability that are used for steel structures such as buildings, bridges, marine vessels, marine structures, construction and industrial machineries, tanks and penstocks, and to methods for manufacturing such steel plates.
  • the invention relates to steel plates having a plate thickness of 100 mm or more and a yield strength of 620 MPa or more.
  • Thick steel plates having a plate thickness of 100 mm or more are usually manufactured by slabbing a large steel ingot produced by an ingot making method, and hot rolling the resultant slab. In this ingot making-slabbing process, densely segregated areas in hot tops and negatively segregated areas in ingot bottoms have to be discarded. This causes low yields, high production costs and long work periods.
  • Non Patent Literature 1 describes a technique in which center porosities are compressed by increasing the rolling shape factor during the hot rolling of a continuously cast slab.
  • Patent Literatures 1 and 2 describe techniques in which center porosities in a continuously cast slab are compressed by working the continuously cast slab with rolls or anvils during its production in the continuous casting machine.
  • Patent Literature 3 describes a technique in which a continuously cast slab is worked into a thick steel plate with a cumulative reduction of not more than 70% in such a manner that the slab is forged before hot rolling so as to compress center porosities.
  • Patent Literature 4 describes a technique in which a continuously cast slab is worked into an ultrathick steel plate by forging and thick plate rolling with a total working reduction of 35 to 67%. In this process, the central area through the plate thickness of the steel is held at a temperature of 1200°C or above for at least 20 hours before forging and the steel is forged with a reduction of not less than 16% so as to eliminate center porosities and also to decrease or remedy the center segregation zone, thereby improving temper brittleness resistance characteristics.
  • Patent Literature 5 describes a technique in which a continuously cast slab is cross forged and then hot rolled to remedy center porosities and center segregation.
  • Patent Literature 6 describes a technique related to a method for manufacturing thick steel plates with a tensile strength of not less than 588 MPa in which a continuously cast slab is held at a temperature of 1200°C or above for at least 20 hours, forged with a reduction of not less than 17%, subjected to thick plate rolling with a total reduction including the forging reduction in the range of 23 to 50%, and quench hardened two times after the thick plate rolling, thereby eliminating center porosities and also decreasing or remedying the center segregation zone.
  • Patent Literature 7 describes a technique related to a method for manufacturing thick steel plates with excellent weldability and ductility in the plate thickness direction wherein a continuously cast slab having a prescribed chemical composition is reheated to 1100°C to 1350°C and is thereafter worked at not less than 1000°C with a strain rate of 0.05 to 3/s and a cumulative working reduction of not less than 15%.
  • Patent Literature 8 describes a high-strength thick steel plate containing, by mass%, C: 0.03 to 0.15%, Si: 0.1 to 0.5%, Mn: 0.5 to 2.0%, P: ⁇ 0.02%, S: ⁇ 0.01%, Al: 0.001 to 0.1%, Ti: 0.005 to 0.02%, Ni: 0.15 to 2% and N: 0.001 to 0.008% and having a balance of iron and unavoidable impurities as chemical components, having a microstructure of a ferrite and/or pearlite structure with bainite as a matrix phase, and having an average circle equivalent diameter of crystal grains with a crystal misorientation angle of 15° or more of 15 ⁇ m or less in the regions of 10% of plate thickness from the front and rear surfaces and of 40 ⁇ m or less in the other region including the center part of plate thickness.
  • Patent Literature 9 describes a method of manufacturing a continuous casting slab and a steel material obtained by working the cast slab.
  • P 0.19 ⁇ Ptotal ⁇ ⁇ ⁇ T / D / 2 ⁇ 4.2
  • Ptotal is a roll reduction amount (%) of the slab and D is the thickness (mm) of the slab before rolling.
  • Patent Literature 10 describes a low-yield-ratio and high-strength thick steel plate and a method of manufacturing the same.
  • the steel includes, by mass%, 0.03 to 0.10% of C, 0.05 to 0.50% of Si, 1.4 to 3.0% of Mn, 0.02% or less of P, 0.0050% or less of S, 0.005 to 0.1% of Al, 0.004 to 0.03% of Ti, 0.0025 to 0.0065% of N, one or more elements of Cu, Ni, Cr, Mo, Nb, V, Ca, a REM, Mg and B as needed, while controlling Ceq to 0.50 to 0.68% and Ti/N to more than 2.0 but less than 4.4, and the balance Fe with unavoidable impurities; wherein a microstructure that contains island-shaped martensites has an average equivalent circle diameter of 1 to 10 ⁇ m and an average aspect ratio of 4.0 or less, in an area fraction of 5 to 18%.
  • the method for manufacturing the steel plate includes the steps of: heating the steel having the above component composition to 1000 to 1250°C; hot-rolling the steel at 800°C or higher; cooling the plate from the Ar3 point or higher to Ar3-350°C to Ar3-100°C at 5 to 100°C/s; temporarily stopping cooling; subsequently re-heating it to the Ac1 point or lower at a heating rate of 0.5°C/s or higher; air-cooling it; and tempering it at 400°C or higher but the Ac1 point or lower, as needed.
  • NPL 1 Tetsu to Hagane (Iron and Steel), Vol. 66 (1980), No. 2, pp. 201-210
  • Non Patent Literature 1 requires that steel plates be rolled with a high rolling shape factor repeatedly in order to achieve good internal quality. However, such rolling is beyond the upper limit of equipment specifications of rolling machines, and consequently manufacturing constraints are encountered.
  • Patent Literatures 1 and 2 have a problem in that large capital investments are necessary for the adaptation of continuous casting facilities, and also have uncertainty about the strength of steel plates obtained in Examples.
  • the techniques of Patent Literatures 3 to 7 are effective for remedying center porosities and for improving center segregation zones.
  • the yield strength of steel plates obtained in Examples of these literatures is less than 620 MPa.
  • Thick steel plates with a yield strength of 620 MPa or above decrease their toughness due to the increase in strength.
  • thick steel plates are cooled at a lower rate in the central area through the plate thickness than in the other areas. In order to ensure strength in such central regions, it is necessary to increase the amounts of alloying elements that are added.
  • the plate thickness of interest is 100 mm or more.
  • the present inventors have carried out extensive studies with respect to thick steel plates having a yield strength of not less than 620 MPa and a plate thickness of not less than 100 mm so as to find a relationship between the microstructure and the strength and toughness in the central area through the plate thickness, as well as to identify the manufacturing conditions that provide such a microstructure.
  • the present invention has been completed based on the obtained findings and further studies. That is, some aspects of the present invention reside in the following.
  • thick steel plates with a plate thickness of not less than 100 mm achieve excellent internal quality in the central area through the plate thickness.
  • the thick steel plates exhibit a yield strength of not less than 620 MPa and have excellent toughness.
  • the inventive manufacturing methods can produce such steel plates.
  • the invention has marked effects in industry by making great contributions to the upsizing of steel structures, improving the safety of steel structures, enhancing the yields, and reducing the production work periods.
  • the invention requires that the microstructure have an average prior austenite grain size of not more than 50 ⁇ m and a martensite and/or bainite phase area fraction of not less than 80% throughout an entire region in the plate thickness direction. Phases other than the martensite and/or bainite phases are not particularly limited.
  • the average prior austenite grain size is the average grain size of prior austenite at the center through the plate thickness.
  • Carbon is an element useful for obtaining the strength required for structural steel at low cost. In order to obtain this effect, the addition of 0.080% or more carbon is necessary. If, on the other hand, more than 0.200% carbon is added, the toughness of base steel and welds is markedly decreased. Thus, the upper limit is limited to 0.200%.
  • the C content is preferably 0.080% to 0.140%.
  • Silicon is added for the purpose of deoxidation. However, the addition of more than 0.40% silicon results in a marked decrease in the toughness of base steel and weld heat affected zones. Thus, the Si content is limited to not more than 0.40%.
  • the Si content is preferably in the range of 0.05% to 0.30%, and more preferably in the range of 0.10% to 0.30%.
  • Manganese is added to ensure the strength of base steel. However, the effect is insufficient when the amount added is less than 0.5%. Adding more than 5.0% manganese not only decreases the toughness of base steel but also facilitates the occurrence of center segregation and increases the size of center porosities in the slabs. Thus, the upper limit is limited to 5.0%.
  • the Mn content is preferably in the range of 0.6 to 2.0%, and more preferably in the range of 0.6 to 1.6%.
  • the toughness of base steel and weld heat affected zones is markedly lowered.
  • the P content is limited to not more than 0.015%.
  • the toughness of base steel and weld heat affected zones is markedly lowered.
  • the S content is limited to not more than 0.0050%.
  • Chromium is an element effective for increasing the strength of base steel. However, the addition of an excessively large amount results in a decrease in weldability. Thus, the Cr content is limited to not more than 3.0%. The Cr content is preferably 0.1% to 2.0%.
  • Nickel is a useful element that increases the strength of steel and the toughness of weld heat affected zones. However, adding more than 5.0% nickel causes a significant decrease in economic efficiency.
  • the upper limit of the Ni content is preferably 5.0% or less.
  • the Ni content is more preferably 0.5% to 4.0%.
  • Titanium forms TiN during heating to effectively suppress the coarsening of austenite and to enhance the toughness of base steel and weld heat affected zones. In order to obtain this effect, 0.005% or more titanium is added. However, the addition of more than 0.020% titanium results in the coarsening of titanium nitride and consequently the toughness of base steel is lowered. Thus, the Ti content is limited to the range of 0.005% to 0.020%. The Ti content is preferably in the range of 0.008% to 0.015%.
  • Aluminum is added to deoxidize molten steel. However, the deoxidation effect is insufficient if the amount added is less than 0.010%. If more than 0.080% aluminum is added, the amount of aluminum dissolved in the base steel is so increased that the toughness of base steel is lowered. Thus, the Al content is limited to the range of 0.010 to 0.080%. The Al content is preferably in the range of 0.030 to 0.080%, and more preferably in the range of 0.030 to 0.060%.
  • Nitrogen has an effect of reducing the size of the microstructure by forming nitrides with elements such as titanium, and thereby enhances the toughness of base steel and weld heat affected zones. If, however, more than 0.0070% nitrogen is added, the amount of nitrogen dissolved in the base steel is so increased that the toughness of base steel is significantly lowered and further the toughness of weld heat affected zones is decreased due to the formation of coarse carbonitride. Thus, the N content is limited to not more than 0.0070%. The N content is preferably not more than 0.0050%, and more preferably not more than 0.0040%.
  • Boron is segregated in austenite grain boundaries and suppresses ferrite transformation from the grain boundaries, thereby exerting an effect of enhancing hardenability.
  • 0.0003% or more boron is added. If the amount added is more than 0.0030%, boron is precipitated as carbonitride to cause a decrease in hardenability and a decrease in toughness.
  • the B content is limited to the range of 0.0003% to 0.0030%.
  • the B content is preferably in the range of 0.0005 to 0.0020%.
  • the aforementioned components constitute the basic chemical composition of the present invention, and the balance is iron and inevitable impurities.
  • the chemical composition may further include one, or two or more of copper, molybdenum and vanadium in order to enhance strength and toughness.
  • Copper increases the strength of steel without causing a decrease in toughness.
  • adding more than 0.50% copper results in the occurrence of cracks on the steel plate surface during hot working.
  • the content of copper, when added, is limited to not more than 0.50%.
  • Molybdenum is an element effective for increasing the strength of base steel. If, however, more than 1.00% molybdenum is added, hardness is increased by the precipitation of alloy carbide and consequently toughness is decreased. Thus, the upper limit of molybdenum, when added, is limited to 1.00%.
  • the Mo content is preferably in the range of 0.20% to 0.80%.
  • Vanadium is effective for increasing the strength and the toughness of base steel, and also effectively decreases the amount of solute nitrogen by being precipitated as VN.
  • adding more than 0.200% vanadium results in a decrease in toughness due to the precipitation of hard VC.
  • the content of vanadium, when added, is limited to not more than 0.200%.
  • the V content is preferably in the range of 0.010 to 0.100%.
  • one, or two or more of calcium and rare earth metals may be added to increase strength and toughness.
  • Calcium is an element useful for controlling the morphology of sulfide inclusions. To obtain its effect, 0.0005% or more calcium needs to be added. If, however, the amount added exceeds 0.0050%, cleanliness is lowered and toughness is decreased. Thus, the content of calcium, when added, is limited to 0.0005 to 0.0050%.
  • the Ca content is preferably in the range of 0.0005% to 0.0025%.
  • rare earth metals Similarly to calcium, rare earth metals have an effect of improving quality through the formation of oxides and sulfides in steel. To obtain this effect, 0.0005% or more rare earth metals need to be added. The effect is saturated after the amount added exceeds 0.0050%. Thus, the content of rare earth metals, when added, is limited to 0.0005 to 0.0050%.
  • the REM content is preferably in the range of 0.0005 to 0.0025%.
  • the temperature "°C” refers to the temperature in the central area through the plate thickness of the slab or the steel plate.
  • casting defects such as center porosities in the steel are eliminated by subjecting the steel to hot working and, after air cooling and reheating or directly without cooling, subjecting the hot-worked steel to hot rolling so as to obtain a desired plate thickness.
  • the temperature of the central area through the plate thickness may be obtained by a method such as simulation calculation using data such as plate thickness, surface temperature and cooling conditions.
  • the temperature in the center through the plate thickness may be obtained by calculating the temperature distribution in the plate thickness direction using a difference method.
  • Heating temperature 1200°C to 1350°C
  • Steel having the aforementioned chemical composition is smelted by a usual known method in a furnace such as a converter furnace, an electric furnace or a vacuum melting furnace, and is continuously cast and rolled into a slab (a steel slab), which is reheated to 1200°C to 1350°C. If the reheating temperature is less than 1200°C, hot working cannot ensure a prescribed cumulative working reduction and further the steel exhibits high deformation resistance during hot working and fails to ensure a sufficient working reduction per pass.
  • a furnace such as a converter furnace, an electric furnace or a vacuum melting furnace
  • the reheating temperature is limited to not less than 1200°C.
  • reheating at a temperature exceeding 1350°C consumes excessively large amounts of energy, and scales formed during the heating raise the probability of surface defects, thus increasing the load in maintenance after the hot working.
  • the upper limit is limited to 1350°C.
  • the hot working described below is performed after the continuously cast slab is worked in the width direction at least until an increase in slab thickness is obtained. This allows center porosities to be compressed more reliably.
  • Width reduction before hot working not less than 100 mm
  • the slab is worked in the width direction before the hot working and thereby the slab thickness is increased to ensure a margin for working.
  • the reduction of width is preferably 100 mm or more because working by 100 mm or more gives rise to a thickness increase in an area that is distant from both ends of the slab width by 1/4 of the slab width. This makes it possible to effectively compress the center porosities of the slab that frequently occur in this area.
  • the width reduction that is 100 mm or more is the total of the width reduction at both ends of the slab width.
  • the working temperature during the hot working is less than 1000°C, the hot working encounters high deformation resistance. Consequently, the load on the hot working machine is increased, and the reliable compression of center porosities fails.
  • the working temperature is limited to not less than 1000°C.
  • the working temperature is preferably 1100°C or more.
  • the cumulative working reduction during the hot working is less than 15%, the compression fails to remedy casting defects such as center porosities in the steel. Thus, the cumulative working reduction is limited to not less than 15%.
  • the cumulative working reduction is the reduction from the increased thickness.
  • the hot working include one or more passes in which the working reduction per pass is 7% or more in order to reliably compress the center porosities. More preferably, the working reduction per pass is in the range of 10% and above.
  • the strain rate during the hot working exceeds 3/s, the hot working encounters high deformation resistance. Consequently, the load on the hot working machine is increased, and the compression of center porosities fails. Thus, the strain rate is limited to not more than 3/s.
  • the hot working requires an extended time to cause a decrease in productivity.
  • the strain rate is preferably not less than 0.01/s. More preferably, the strain rate is in the range of 0.05/s to 1/s.
  • the hot working may be performed by a known method such as hot forging or hot rolling. Hot forging is preferable from the viewpoints of economic efficiency and high degree of freedom.
  • the central area through the plate thickness achieves stable enhancement in elongation in a tensile test.
  • the hot-worked steel is subjected to hot rolling so as to obtain a desired plate thickness.
  • the hot rolling is performed after air cooling and reheating or is carried out directly without cooling.
  • the hot-worked steel is hot rolled into a steel plate having a desired plate thickness.
  • the steel plate is then subjected to quench hardening and tempering in order to ensure that a yield strength of not less than 620 MPa and good toughness are exhibited even in the central area through the plate thickness of the resultant steel plate.
  • the hot-worked steel is heated to or above the Ac3 transformation point.
  • the austenite structure is coarsened to cause a decrease in toughness.
  • the reheating temperature is limited to the Ac3 point to 1200°C.
  • the Ac3 transformation point is a value calculated using Expression (2) below.
  • Ac 3 937.2 ⁇ 476.5 ⁇ C + 56 ⁇ Si ⁇ 19.7 ⁇ Mn ⁇ 16.3 ⁇ Cu ⁇ 26.6 ⁇ Ni ⁇ 4.9 ⁇ Cr + 38.1 ⁇ Mo + 124.8 ⁇ V + 136.3 ⁇ Ti + 198.4 ⁇ Al + 3315 ⁇ B
  • the element symbols indicate the contents (mass%) of the respective alloying elements.
  • Rolling reduction per pass two or more passes with 4% or more reduction
  • Rolling with a reduction per pass of 4% or more ensures that the recrystallization of austenite is promoted over the entire region through the plate thickness.
  • the austenite grains attain small and regular sizes.
  • fine prior austenite grains are formed by quench hardening and tempering, and consequently toughness may be enhanced.
  • the rolling reduction per pass is 6% or more.
  • quench hardening and tempering are performed in the invention.
  • the hot-rolled plate is allowed to cool naturally, reheated to the Ac3 point to 1050°C, and quenched from a temperature of not less than the Ar3 point to 350°C or below.
  • the reheating temperature is limited to 1050°C or below because reheating at a high temperature exceeding 1050°C causes the austenite grains to be coarsened and thus results in a marked decrease in the toughness of base steel.
  • the Ar3 transformation point is a value calculated using Expression (3) below.
  • Ar 3 910 ⁇ 310 ⁇ C ⁇ 80 ⁇ Mn ⁇ 20 ⁇ Cu ⁇ 15 ⁇ Cr ⁇ 55 ⁇ Ni ⁇ 80 ⁇ Mo
  • the element symbols indicate the contents (mass%) of the respective alloying elements.
  • a general quenching method in industry is water cooling.
  • the cooling rate is desirably as high as possible, any cooling methods other than water cooling may be adopted.
  • Exemplary methods include gas cooling.
  • the tempering temperature is 450°C to 700°C. Tempering at less than 450°C produces a small effect in removing residual stress. If, on the other hand, the temperature exceeds 700°C, various carbides are precipitated and the microstructure of the base steel is coarsened to cause a marked decrease in strength and toughness. Thus, the tempering temperature is limited to 450°C to 700°C.
  • quench hardening is performed a plurality of times for the purpose of increasing the strength and the toughness of steel, it is necessary that the final quench hardening be performed in such a manner that the steel is heated to the Ac3 point to 1050°C, quenched to 350°C or below and tempered at 450°C to 700°C.
  • Samples having a 10 ⁇ 10 (mm) observation area were obtained from the surface and the center through the plate thickness of an L cross section of the steel as quenched.
  • the microstructure was exposed with a Nital etching solution.
  • Five fields of view were observed with a ⁇ 200 optical microscope, and the images were analyzed to measure fractions in the microstructure.
  • L cross sectional observation samples were etched with picric acid to expose the prior ⁇ grain boundaries, and the images were analyzed to measure the circular equivalent diameters of the prior ⁇ grains, the results being averaged.
  • a sample 12.5 in thickness and 50 in length (mm) was obtained from the central area through the plate thickness.
  • the sample was inspected for 100 ⁇ m or larger porosities with an optical microscope.
  • Round bars as tensile test pieces were obtained from the central area through the plate thickness of each of the steel plates, along a direction perpendicular to the rolling direction. The test pieces were tested to measure the yield strength (YS), the tensile strength (TS) and the total elongation (t. El).
  • Three round bars as tensile test pieces (diameter 10 mm) were obtained along the direction of the plate thickness of each steel plate. The reduction of area after fracture was measured, and the results were averaged.
  • Tables 2 to 5 describe the manufacturing conditions and the results of the above tests. From the tables, the steel plates of the steels Nos. 1 to 16 (the specimens Nos. 1 to 16) which satisfied the chemical composition of steel according to the present invention achieved YS of not less than 620 MPa, TS of not less than 720 MPa, t. El of not less than 16%, base steel toughness ( V E -40 ) of not less than 70 J, and a reduction of area of not less than 25%. Thus, the base steels exhibited excellent strength and toughness.
  • the characteristics of base steel were inferior and corresponded to one or more of YS of less than 620 MPa, TS of less than 720 MPa, t. El of less than 16% and toughness ( V E -40 ) of less than 70 J.
  • the steel No. 28 failed to satisfy the Ceq requirement, and consequently the martensite and/or bainite fraction in the central area through the plate thickness was less than 80% to cause a decrease in yield strength.
  • the corresponding steel plate did not achieve the target strength.

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Claims (6)

  1. Verfahren zur Herstellung einer dicken, hochzähen, hochfesten Stahlplatte mit einer Plattendicke von nicht weniger als 100 mm,
    wobei die Stahlplatte eine Mikrostruktur beinhaltet, die, über eine gesamte Region in der Plattendickenrichtung, eine durchschnittliche Korngröße des früheren Austenits von nicht mehr als 50 µm und einen Martensit- und/oder Bainitphasen-Flächenanteil von nicht weniger als 80% aufweist,
    wobei eine kontinuierlich gegossene Bramme auf 1200°C bis 1350°C aufgeheizt wird, bei nicht weniger als 1000°C mit einer Umformgeschwindigkeit von nicht mehr als 3/s und einer kumulativen Verarbeitungsreduktion von nicht weniger als 15% warmverarbeitet wird, anschließend direkt Warmwalzen unterzogen wird oder luftgekühlt und wieder auf den Ac3-Punkt bis 1200°C aufgeheizt wird bevor sie Warmwalzen unterzogen wird, wobei das Warmwalzen zumindest zwei oder mehr Stiche mit einer Walzreduktion pro Stich von nicht weniger als 4% beinhaltet, luftgekühlt wird, auf den Ac3-Punkt bis 1050°C aufgeheizt wird, auf 350°C oder darunter abgeschreckt wird und bei 450°C bis 700°C getempert wird, wobei die Temperaturen Temperaturen in dem zentralen Bereich durch die Dicke der Bramme oder Platte sind,
    wobei die kontinuierlich gegossene Bramme, in Massen%, aus C: 0,08 bis 0,20%, Si: nicht mehr als 0,40%, Mn: 0,5 bis 5,0%, P: nicht mehr als 0,015%, S: nicht mehr als 0,0050%, Cr: nicht mehr als 3,0%, Ni: nicht mehr als 5,0%, Ti: 0,005% bis 0,020%, Al: 0,010 bis 0,080%, N: nicht mehr als 0,0070%, B: 0,0003 bis 0,0030%, optional einem oder zweien oder mehreren aus Cu: nicht mehr als 0,50%, Mo: nicht mehr als 1,00% und V: nicht mehr als 0,200%, und optional einem oder beiden aus Ca: 0,0005 bis 0,0050% und REM: 0,0005 bis 0,0050% und als Rest aus Fe und unvermeidbaren Verunreinigungen besteht, wobei die kontinuierlich gegossene Bramme die durch den Ausdruck (1) repräsentierte Beziehung erfüllt: Ceq IIW = C + Mn / 6 + Cu + Ni / 15 + Cr + Mo + V / 5 ≥ 0,57
    Figure imgb0012
     wobei die Legierungselementsymbole die jeweiligen Gehalte (Massen%) anzeigen und 0 in Abwesenheit sind.
  2. Verfahren zur Herstellung einer dicken, hochzähen, hochfesten Stahlplatte gemäß Anspruch 1, wobei die Bramme, in Massen%, eines oder beide aus Ca: 0,0005 bis 0,0050% und REM: 0,0005 bis 0,0050% beinhaltet.
  3. Verfahren zur Herstellung einer dicken, hochzähen, hochfesten Stahlplatte gemäß Anspruch 1 oder 2, wobei die kontinuierlich gegossene Bramme verarbeitet wird, um die Breite um nicht weniger als 100 mm vor dem Warmverarbeiten zu reduzieren, und anschließend mit einer Umformgeschwindigkeit von nicht mehr als 3/s und einer kumulativen Verarbeitungsreduktion von nicht weniger als 15% warmverarbeitet wird.
  4. Dicke, hochzähe und hochfeste Stahlplatte erhältlich durch das Verfahren gemäß einem der Ansprüche 1 bis 3,
    wobei die Stahlplatte eine Plattendicke von nicht weniger als 100 mm aufweist und
    eine Zusammensetzung aufweist, die, in Massen%, aus C: 0,08 bis 0,20%, Si: nicht mehr als 0,40%, Mn: 0,5 bis 5,0%, P: nicht mehr als 0,015%, S: nicht mehr als 0,0050%, Cr: nicht mehr als 3,0%, Ni: nicht mehr als 5,0%, Ti: 0,005% bis 0,020%, Al: 0,010 bis 0,080%, N: nicht mehr als 0,0070%, B: 0,0003 bis 0,0030%, optional einem oder zweien oder mehreren aus Cu: nicht mehr als 0,50%, Mo: nicht mehr als 1,00% und V: nicht mehr als 0,200%, und optional einem oder beiden aus Ca: 0,0005 bis 0,0050% und REM: 0,0005 bis 0,0050% und als Rest aus Fe und unvermeidbaren Verunreinigungen besteht und wobei Zusammensetzung die durch den Ausdruck (1) repräsentierte Beziehung erfüllt: Ceq IIW = C + Mn / 6 + Cu + Ni / 15 + Cr + Mo + V / 5 ≥ 0,57
    Figure imgb0013
     wobei die Legierungselementsymbole die jeweiligen Gehalte (Massen%) anzeigen und 0 in Abwesenheit sind, und
    wobei die Stahlplatte eine Mikrostruktur aufweist, die, über eine gesamte Region in der Plattendickenrichtung, eine durchschnittliche Korngröße des früheren Austenits von nicht mehr als 50 µm und einen Martensit- und/oder Bainitphasen-Flächenanteil von nicht weniger als 80% aufweist.
  5. Dicke, hochzähe und hochfeste Stahlplatte gemäß Anspruch 4, wobei die Streckgrenze nicht weniger als 620 MPa beträgt.
  6. Dicke, hochzähe und hochfeste Stahlplatte gemäß Anspruch 4 oder 5, wobei die Flächenreduktion nach Bruch in einem Zugtest in der Richtung der Plattendicke der Stahlplatte nicht weniger als 25% beträgt.
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KR20150114574A (ko) 2015-10-12
EP2942414A4 (de) 2016-04-20
JPWO2014141697A1 (ja) 2017-02-16
KR101716265B1 (ko) 2017-03-14
CN105008570B (zh) 2017-12-19
US20160010192A1 (en) 2016-01-14
CA2899570C (en) 2019-04-30
US10000833B2 (en) 2018-06-19
JP5928654B2 (ja) 2016-06-01
SG11201505732RA (en) 2015-08-28
CA2899570A1 (en) 2014-09-18
EP2942414A1 (de) 2015-11-11
WO2014141697A1 (ja) 2014-09-18
KR101806340B1 (ko) 2017-12-07
CN105008570A (zh) 2015-10-28

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